Films having desirable mechanical properties and articles made therefrom

ABSTRACT

Disclosed herein is a film comprising a layer that comprises a polyethylene composition comprising the reaction product of ethylene and optionally one or more alpha-olefin comonomers, wherein said polyethylene composition is characterized by the following properties: a melt index, I2, measured according to ASTM D1238 (2.16 kg, 190 C), of from 0.5 to 10 g/10 min; a density (measured according to ASTM D792) of less than 0.935 g/cm3; a melt flow ratio, I10/I2, wherein I10 is measured according to ASTM D1238 (10 kg, 190 C) of from 6.0 to 7.5; a molecular weight distribution (Mw/Mn) of from 2.8 to 3.9; and a vinyl unsaturation of greater than 0.12 vinyls per one thousand carbon atoms, and a low density polyethylene.

FIELD

Embodiments of the present disclosure generally relate to films having desirable mechanical properties and to articles made from such films. Examples of such articles include flexible packages.

BACKGROUND

Polyethylene films are widely used in a variety of products including, for example, flexible packaging applications. Flexible package films may typically be made from blends of linear low density polyethylene (LLDPE) and low density polyethylene (LDPE). A number of mechanical properties are important for films to be used in flexible packaging applications including, for example, dart impact resistance, puncture, and tear. Existing films for flexible packaging can sometimes provide some desirable mechanical properties, but at the expense of one or more other properties.

Accordingly, films having a combination of high puncture and dart impact resistance without reducing tear resistance are desired.

SUMMARY

Disclosed in embodiments herein are films which provide one or more desirable mechanical properties or a combination of properties. In some embodiments, films of the present invention provide a desirable combination of puncture, dart impact resistance, and tear resistance. Such films, in some embodiments, can be used in articles such as flexible packages.

In one aspect, films of the present invention comprise a layer comprising (a) 50% or more by weight of a polyethylene composition comprising the reaction product of ethylene and optionally one or more alpha-olefin comonomers, wherein said polyethylene composition is characterized by the following properties: a melt index, I₂, measured according to ASTM D1238 (2.16 kg, 190° C.), of from 0.5 to 10 g/10 min; a density (measured according to ASTM D792) of less than 0.935 g/cm³; a melt flow ratio, I₁₀/I₂, wherein I₁₀ is measured according to ASTM D1238 (10 kg, 190° C.) of from 6.0 to 7.5; a molecular weight distribution (M_(w)/M_(n)) of from 2.8 to 3.9; and a vinyl unsaturation of greater than 0.12 vinyls per one thousand carbon atoms; and (b) 50% or less by weight of a low density polyethylene.

Also disclosed herein are articles comprising a film according to any of the embodiments disclosed herein. For example, in one aspect, films used in such articles comprise a layer comprising (a) 50% or more by weight of a polyethylene composition comprising the reaction product of ethylene and optionally one or more alpha-olefin comonomers, wherein said polyethylene composition is characterized by the following properties: a melt index, I₂, measured according to ASTM D1238 (2.16 kg, 190° C.), of from 0.5 to 10 g/10 min; a density (measured according to ASTM D792) of less than 0.935 g/cm³; a melt flow ratio, I₁₀/I₂, wherein I₁₀ is measured according to ASTM D1238 (10 kg, 190° C.) of from 6.0 to 7.5; a molecular weight distribution (M_(w)/M_(n)) of from 2.8 to 3.9; and a vinyl unsaturation of greater than 0.12 vinyls per one thousand carbon atoms; and (b) 50% or less by weight of a low density polyethylene.

These and other embodiments are described in more detail in the Detailed Description.

DETAILED DESCRIPTION

Unless stated to the contrary, implicit from the context, or customary in the art, all parts and percentages are based on weight, all temperatures are in ° C., and all test methods are current as of the filing date of this disclosure.

The term “composition,” as used herein, refers to a mixture of materials which comprises the composition, as well as reaction products and decomposition products formed from the materials of the composition.

Reference will now be made in detail to embodiments of films and articles, examples of which are further described below. In some embodiments, the films may have a desirable combination of puncture, dart impact resistance, and tear resistance and may be used in flexible packages. It is noted, however, that this is merely an illustrative implementation of the embodiments disclosed herein. The embodiments are applicable to other technologies that are susceptible to similar problems as those discussed above. The film may be a monolayer film or a multilayer film. As used herein, “multilayer film” refers to a film having two or more layers that are at least partially contiguous and preferably, but optionally, coextensive.

In some embodiments, a film of the present invention comprises a layer, the layer comprising (a) 50% or more by weight of a polyethylene composition comprising the reaction product of ethylene and optionally one or more alpha-olefin comonomers, wherein said polyethylene composition is characterized by the following properties: a melt index, I₂, measured according to ASTM D1238 (2.16 kg, 190° C.), of from 0.5 to 10 g/10 min; a density (measured according to ASTM D792) of less than 0.935 g/cm³; a melt flow ratio, I₁₀/I₂, wherein I₁₀ is measured according to ASTM D1238 (10 kg, 190° C.) of from 6.0 to 7.5; a molecular weight distribution (M_(w)/M_(n)) of from 2.8 to 3.9; and a vinyl unsaturation of greater than 0.12 vinyls per one thousand carbon atoms; and (b) 50% or less by weight of a low density polyethylene.

In some embodiments, the polyethylene composition is formed in the presence of a catalyst composition comprising a multi-metallic procatalyst via solution polymerization in at least one reactor. In some further embodiments, the solution polymerization occurs in a single reactor. The polyethylene composition, in some embodiments, has a metal catalyst residual of greater than or equal to 1 parts by combined weight of at least three metal residues per one million parts of polyethylene polymer, wherein the at least three metal residues are selected from the group consisting of titanium, zirconium, hafnium, vanadium, niobium, tantalum, chromium, molybdenum, tungsten, and combinations thereof, and wherein each of the at least three metal residues is present at greater than or equal to 0.2 ppm. In some embodiments, the polyethylene composition has an Al:Ti ratio of from 6 to 15.

In some embodiments, the film comprises 5 to 30% by weight of the low density polyethylene. The low density polyethylene, in some embodiments, has a melt index, I₂, of 0.1 to 5 g/10 minutes.

In embodiments herein, the film layer comprises 50% or more by weight of a polyethylene composition. The film layer comprises from 50 to 99 percent, 55 to 99 percent, 60 to 99 percent, 65 to 99 percent, 70 to 99 percent, 75 to 99 percent, 80 to 99 percent, 85 to 99 percent, 90 to 99 percent, or 95 to 99 percent, by total weight of polymers present in the film layer, of the polyethylene composition.

In some embodiments, films of the present invention comprise a layer comprising (a) 70% or more by weight of a polyethylene composition comprising the reaction product of ethylene and optionally one or more alpha-olefin comonomers, wherein said polyethylene composition is characterized by the following properties: a melt index, I₂, measured according to ASTM D1238 (2.16 kg, 190° C.), of from 0.5 to 2 g/10 min; a density (measured according to ASTM D792) of less than 0.935 g/cm³; a melt flow ratio, I₁₀/I₂, wherein I₁₀ is measured according to ASTM D1238 (10 kg, 190° C.) of from 6.5 to 7.5; a molecular weight distribution (M_(w)/M_(n)) of from 2.8 to 3.9; and a vinyl unsaturation of greater than 0.12 vinyls per one thousand carbon atoms; and (b) 30% or less by weight of a low density polyethylene.

The polyethylene composition comprises the reaction product of ethylene and optionally one or more alpha-olefin comonomers. The polyethylene composition comprises greater than 50 wt. % of the units derived from ethylene and less than 30 wt. % of the units derived from one or more alpha-olefin comonomers. In some embodiments, the polyethylene composition comprises (a) greater than or equal to 55%, for example, greater than or equal to 60%, greater than or equal to 65%, greater than or equal to 70%, greater than or equal to 75%, greater than or equal to 80%, greater than or equal to 85%, greater than or equal to 90%, greater than or equal to 92%, greater than or equal to 95%, greater than or equal to 97%, greater than or equal to 98%, greater than or equal to 99%, greater than or equal to 99.5%, from greater than 50% to 99%, from greater than 50% to 97%, from greater than 50% to 94%, from greater than 50% to 90%, from 70% to 99.5%, from 70% to 99%, from 70% to 97% from 70% to 94%, from 80% to 99.5%, from 80% to 99%, from 80% to 97%, from 80% to 94%, from 80% to 90%, from 85% to 99.5%, from 85% to 99%, from 85% to 97%, from 88% to 99.9%, 88% to 99.7%, from 88% to 99.5%, from 88% to 99%, from 88% to 98%, from 88% to 97%, from 88% to 95%, from 88% to 94%, from 90% to 99.9%, from 90% to 99.5% from 90% to 99%, from 90% to 97%, from 90% to 95%, from 93% to 99.9%, from 93% to 99.5% from 93% to 99%, or from 93% to 97%, by weight, of the units derived from ethylene; and (b) optionally, less than 30 percent, for example, less than 25 percent, or less than 20 percent, less than 18%, less than 15%, less than 12%, less than 10%, less than 8%, less than 5%, less than 4%, less than 3%, less than 2%, less than 1%, from 0.1 to 20%, from 0.1 to 15%, 0.1 to 12%, 0.1 to 10%, 0.1 to 8%, 0.1 to 5%, 0.1 to 3%, 0.1 to 2%, 0.5 to 12%, 0.5 to 10%, 0.5 to 8%, 0.5 to 5%, 0.5 to 3%, 0.5 to 2.5%, 1 to 10%, 1 to 8%, 1 to 5%, 1 to 3%, 2 to 10%, 2 to 8%, 2 to 5%, 3.5 to 12%, 3.5 to 10%, 3.5 to 8%, 3.5% to 7%, or 4 to 12%, 4 to 10%, 4 to 8%, or 4 to 7%, by weight, of units derived from one or more α-olefin comonomers. The comonomer content may be measured using any suitable technique, such as techniques based on nuclear magnetic resonance (“NMR”) spectroscopy, and, for example, by 13C NMR analysis as described in U.S. Pat. No. 7,498,282, which is incorporated herein by reference.

Suitable comonomers may include alpha-olefin comonomers, typically having no more than 20 carbon atoms. The one or more alpha-olefins may be selected from the group consisting of C₃-C₂₀ acetylenically unsaturated monomers and C₄-C₁₈ diolefins. Those skilled in the art will understand that the selected monomers are desirably those that do not destroy conventional Ziegler-Natta catalysts. For example, the alpha-olefin comonomers may have 3 to 10 carbon atoms, or 3 to 8 carbon atoms. Exemplary alpha-olefin comonomers include, but are not limited to, propylene, 1-butene, 1-pentene, 1-hexene, 1-heptene, 1-octene, 1-nonene, 1-decene, and 4-methyl-1-pentene. The one or more alpha-olefin comonomers may, for example, be selected from the group consisting of propylene, 1-butene, 1-hexene, and 1-octene; or in the alternative, from the group consisting of 1-butene, 1-hexene and 1-octene. In some embodiments, the polyethylene composition comprises greater than 0 wt. % and less than 30 wt. % of units derived from one or more of octene, hexene, or butene comonomers.

In some embodiments, the polyethylene composition is formed in the presence of a catalyst composition comprising a multi-metallic procatalyst via solution polymerization in at least one reactor. In other embodiments, the polyethylene composition is formed in the presence of a catalyst composition comprising a multi-metallic procatalyst comprising of three or more transition metals via solution polymerization in at least one reactor. In some embodiments, the solution polymerization occurs in a single reactor. The multi-metallic procatalyst used in producing the reaction product is at least trimetallic, but may also include more than three transition metals, and thus may in one embodiment be defined more comprehensively as multi-metallic. These three, or more, transition metals are selected prior to production of the catalyst. In a particular embodiment, the multi-metal catalyst comprises titanium as one element.

The catalyst compositions may be prepared beginning first with preparation of a conditioned magnesium halide-based support. Preparation of a conditioned magnesium halide-based support begins with selecting an organomagnesium compound or a complex including an organomagnesium compound. Such compound or complex is desirably soluble in an inert hydrocarbon diluent. The concentrations of components are preferably such that when the active halide, such as a metallic or non-metallic halide, and the magnesium complex are combined, the resultant slurry is from about 0.005 to about 0.25 molar (moles/liter) with respect to magnesium. Examples of suitable inert organic diluents include liquefied ethane, propane, isobutane, n-butane, n-hexane, the various isomeric hexanes, isooctane, paraffinic mixtures of alkanes having from 5 to 10 carbon atoms, cyclohexane, methylcyclopentane, dimethylcyclohexane, dodecane, industrial solvents composed of saturated or aromatic hydrocarbons such as kerosene, naphthas, and combinations thereof, especially when freed of any olefin compounds and other impurities, and especially those having boiling points in the range from about −50° C. to about 200° C. Also included as suitable inert diluents are ethylbenzene, cumene, decalin and combinations thereof.

Suitable organomagnesium compounds and complexes may include, for example, magnesium C₂-C₈ alkyls and aryls, magnesium alkoxides and aryloxides, carboxylated magnesium alkoxides, and carboxylated magnesium aryloxides. Preferred sources of magnesium moieties may include the magnesium C₂-C₈ alkyls and C₁-C₄ alkoxides. Such organomagnesium compound or complex may be reacted with a metallic or non-metallic halide source, such as a chloride, bromide, iodide, or fluoride, in order to make a magnesium halide compound under suitable conditions. Such conditions may include a temperature ranging from −25° C. to 100° C., alternatively, 0° C. to 50° C.; a time ranging from 1 to 12 hours, alternatively, from 4 to 6 hours; or both. The result is a magnesium halide based support.

The magnesium halide support is then reacted with a selected conditioning compound containing an element selected from the group consisting of boron, aluminum, gallium, indium and tellurium, under conditions suitable to form a conditioned magnesium halide support. This compound and the magnesium halide support are then brought into contact under conditions sufficient to result in a conditioned magnesium halide support. Such conditions may include a temperature ranging from 0° C. to 50° C., or alternatively, from 25° C. to 35° C.; a time ranging from 4 to 24 hours, or alternatively, from 6 to 12 hours; or both. The conditioning compound has a molar ratio constitution that is specific and which is believed to be an important feature in ensuring the desirable catalyst performance. Specifically, the procatalyst desirably exhibits a molar ratio of the magnesium to the conditioning compound that ranges from 3:1 to 6:1. Without wishing to be bound by any theory of mechanism, it is suggested that this aging serves to facilitate or enhance adsorption of additional metals onto the support.

Once the conditioned support is prepared and suitably aged, it is brought into contact with a titanium compound which may be added individually or as a mixture with the “second metal”. In certain preferred embodiments titanium halides or alkoxides, or combinations thereof, may be selected. Conditions may include a temperature within the range from 0° C. to 50° C., alternatively from 25° C. to 35° C.; a time from 3 hours to 24 hours, alternatively from 6 hours to 12 hours; or both. The result of this step is adsorption of at least a portion of the titanium compound onto the conditioned magnesium halide support.

Finally, one or two additional metals, referred to herein as “the second metal” and “the third metal” for convenience, will also be adsorbed onto the magnesium-based support, The “second metal” and the “third metal” are independently selected from zirconium (Zr), hafnium (Hf), vanadium (V), niobium (Nb), tantalum (Ta), chromium (Cr), molybdenum (Mo), and tungsten (W). These metals may be incorporated in any of a variety of ways known to those skilled in the art, but generally contact between the conditioned magnesium based halide support including titanium and the selected second and third metals, in, e.g., liquid phase such as an appropriate hydrocarbon solvent, will be suitable to ensure deposition of the additional metals to form what may now be referred to as the “procatalyst,” which is a multi-metallic procatalyst.

The multi-metallic procatalyst has a molar ratio constitution that is specific and which is believed to be an important feature in ensuring the desirable polymer properties that may be attributed to the catalyst made from the procatalyst. Specifically, the procatalyst desirably exhibits a molar ratio of the magnesium to a combination of the titanium and the second and third metals that ranges from 30:1 to 5:1; under conditions sufficient to form a multi-metallic procatalyst. Thus, the overall molar ratio of magnesium to titanium ranges from 8:1 to 80:1. In some embodiments, the Al:Ti ratio is from 6 to 15, 7 to 14, 7 to 13, 8 to 13, 9 to 13, or 9 to 12.

Once the procatalyst has been formed, it may be used to form a final catalyst by combining it with a cocatalyst consisting of at least one organometallic compound such as an alkyl or haloalkyl of aluminum, an alkylaluminum halide, a Grignard reagent, an alkali metal aluminum hydride, an alkali metal borohydride, an alkali metal hydride, an alkaline earth metal hydride, or the like. The formation of the final catalyst from the reaction of the procatalyst and the organometallic cocatalyst may be carried out in situ, or just prior to entering the polymerization reactor. Thus, the combination of the cocatalyst and the procatalyst may occur under a wide variety of conditions. Such conditions may include, for example, contacting them under an inert atmosphere such as nitrogen, argon or other inert gas at temperatures in the range from 0° C. to 250° C., preferably from 15° C. to 200° C. In the preparation of the catalytic reaction product, it is not necessary to separate hydrocarbon soluble components from hydrocarbon insoluble components. Time for contact between the procatalyst and cocatalyst may desirably range, for example, from 0 to 240 seconds, preferably from 5 to 120 seconds. Various combinations of these conditions may be employed.

In embodiments described herein, the polyethylene composition may have a metal catalyst residual of greater than or equal to 1 parts by combined weight of at least three metal residues per one million parts of polyethylene polymer, wherein the at least three metal residues are selected from the group consisting of titanium, zirconium, hafnium, vanadium, niobium, tantalum, chromium, molybdenum, tungsten, and combinations thereof, and wherein each of the at least three metal residues is present at greater than or equal to 0.2 ppm, for example, in the range of from 0.2 to 5 ppm. All individual values and subranges from greater than or equal to 0.2 ppm are included herein and disclosed herein; for example, the polyethylene composition may further comprise greater than or equal to 2 parts by combined weight of at least three metal residues remaining from the multi-metallic polymerization catalyst per one million parts of the polyethylene composition.

In embodiments described herein, the polyethylene composition may have a metal catalyst residual of greater than or equal to 1 parts by combined weight of at least three metal residues per one million parts of polyethylene polymer, wherein the at least three metal residues are selected from the group consisting of titanium, zirconium, hafnium, vanadium, niobium, tantalum, chromium, molybdenum, tungsten, and combinations thereof, and wherein each of the at least three metal residues is present at greater than or equal to 0.4 ppm, for example, in the range of from 0.4 to 5 ppm. All individual values and subranges from greater than or equal to 0.4 ppm are included herein and disclosed herein; for example, the polyethylene composition may further comprise greater than or equal to 2 parts by combined weight of at least three metal residues remaining from the multi-metallic polymerization catalyst per one million parts of the polyethylene composition.

In some embodiments, the polyethylene composition comprises at least 0.75 ppm of V (Vanadium). All individual values and subranges from at least 0.75 ppm of V are included and disclosed herein; for example the lower limit of the V in the polyethylene composition may be 0.75, 1, 1.1, 1.2, 1.3 or 1.4 ppm to an upper limit of the V in the polyethylene composition may be 5, 4, 3, 2, 1.9, 1.8, 1.7, 1.6, 1.5, or 1 ppm. The vanadium catalyst metal residual concentration for the polyethylene composition can be measured using the Neutron Activation Method for Metals described below.

In some embodiments, the polyethylene composition comprises at least 0.3 ppm of Zr (Zirconium). All individual values and subranges of at least 0.3 ppm of Zr are included and disclosed herein; for example the lower limit of the Zr in the polyethylene composition may be 0.3, 0.4, 0.5, 0.6 or 0.7 ppm. In yet another embodiment, the upper limit of the Zr in the polyethylene composition may be 5, 4, 3, 2, 1, 0.9, 0.8 or 0.7 ppm. The zirconium catalyst metal residual concentration for the polyethylene composition can be measured using the Neutron Activation Method for Metals described below.

In embodiments described herein, the polyethylene composition has a density of less than 0.935 g/cm³. In some embodiments, the polyethylene composition has a density of 0.900 g/cm³ to less than 0.935 g/cm³. All individual values and subranges of 0.900 g/cm³ up to 0.935 g/cm³ are included and disclosed herein. For example, in some embodiments, the polyethylene composition may have a density ranging from a lower limit of 0.900, 0.903, 0.905, 0.910, 0.912, 0.915, 0.917, 0.918, 0.920, 0.922, 0.925, 0.926, 0.927, or 0.930 g/cm³ to an upper limit of 0.920, 0.922, 0.925, 0.928, 0.930, 0.932, 0.934, or 0.935 g/cm³. In other embodiments, the polyethylene composition may have a density of 0.910 to 0.930 g/cm³, 0.915 to 0.928 g/cm³, 0.910 to 0.924 g/cm³, 0.915 to 0.925 g/cm³, 0.912 to 0.928 g/cm³, or 0.916 to 0.932 g/cm³. Density may be measured in accordance with ASTM D792.

In embodiments described herein, the polyethylene composition has a melt index, I₂, of 0.5 g/10 min to 10 g/10 min. All individual values and subranges of at least 0.5 g/10 min to 10 g/10 min are included and disclosed herein. For example, in some embodiments, the polyethylene composition may have melt index, I₂, ranging from a lower limit of 0.5, 0.6, 0.7, 0.8, 0.9, 1.0, 1.5, 2.0, 2.5, 3.0, 3.4, 3.5, 4.0, or 4.5 to an upper limit of 10, 9, 8, 7, 6, 5, 4, 3, or 2 g/10 min. In other embodiments, the polyethylene composition may have a melt index, I₂, of 0.5 g/10 min to 7 g/10 min, 0.5 g/10 min to 5 g/10 min, or 0.5 g/10 min to 2.5 g/10 min. In some embodiments, the polyethylene composition may have a melt index, I₂, of 0.5 g/10 min to 2.0 g/10 min, 0.5 g/10 min to 1.8 g/10 min, 0.5 g/10 min to 1.5 g/10 min, or 0.5 g/10 min to 1.3 g/10 min. In further embodiments, the polyethylene composition may have a melt index, I₂, of 1.0 g/10 min to 10 g/10 min, 1.0 g/10 min to 5 g/10 min, or 1.0 g/10 min to 4.5 g/10 min. Melt index, I₂, may be measured in accordance with ASTM D1238 (190° C. and 2.16 kg).

In embodiments described herein, the polyethylene composition has a melt flow ratio, I₁₀/I₂, of from 6.0 to 7.5. All individual values and subranges of from 6.0 to 7.5 are included and disclosed herein. For example, in some embodiments, the polyethylene composition may have a melt flow ratio, I₁₀/I₂, ranging from a lower limit of 6.0, 6.1, 6.2, 6.3, 6.4, 6.5, 6.6, or 6.7 to an upper limit of 7.5, 7.4, or 7.35. In other embodiments, the polyethylene composition may have a melt flow ratio, I₁₀/I₂, of from 6.1 to 7.5, 6.2 to 7.5, 6.3 to 7.5, 6.4 to 7.5, or 6.5 to 7.5. Melt index, I₁₀, may be measured in accordance with ASTM D1238 (190° C. and 10.0 kg).

In embodiments described herein, the polyethylene composition has a molecular weight distribution (M_(w)/M_(n)) of from 2.8 to 3.9. All individual values and subranges of from 2.8 to 3.9 are included and disclosed herein. For example, the polyethylene composition may have an M_(w)/M_(n) ratio from a lower limit of 2.8, 2.9, 3.0, 3.1, 3.2, or 3.3 to an upper limit of 3.9, 3.8, 3.7, 3.6, 3.5, 3.4, 3.3, 3.2, 3.1, 3.0, or 2.9. In some embodiments, the polyethylene composition may have an M_(w)/M_(n) ratio of from 2.8 to 3.9, 2.9 to 3.9, 3.0 to 3.9, 3.1 to 3.9, 3.2 to 3.9, 3.3 to 3.9, or 3.5 to 3.8. Molecular weight distribution can be described as the ratio of weight average molecular weight (M_(w)) to number average molecular weight (M_(n)) (i.e., M_(w)/M_(n)), and can be measured by gel permeation chromatography techniques.

In embodiments described herein, the polyethylene composition has number average molecular weight (M_(n)) from 25,000 to 50,000 g/mol, from 30,000 to 40,000 g/mol in some embodiments, from 31,000 to 36,000 g/mol in some embodiments.

In embodiments described herein, the polyethylene composition has weight average molecular weight (M_(w)) from 110,000 to 140,000 g/mol, from 115,000 to 135,000 g/mol in some embodiments, from 118,000 to 130,000 g/mol in some embodiments.

In embodiments described herein, the polyethylene composition has z-average molecular weight (M_(t)) from 380,000 to 450,000 g/mol, from 390,000 to 440,000 g/mol in some embodiments, from 395,000 to 435,000 g/mol in some embodiments.

In embodiments described herein, the polyethylene composition has M_(z)/M_(w) (ratio of z-average molecular weight (M_(z)) to weight average molecular weight (M_(w))) from 2.0 to 5.0, from 3.0 to 4.0 in some embodiments, from 3.2 to 3.5 in some embodiments.

In embodiments described herein, the polyethylene composition has M_(z)/M_(n) (ratio of z-average molecular weight (M_(z)) to number average molecular weight (M_(n))) from 10.0 to 14.0, from 11.0 to 13.5 in some embodiments, from 11.5 to 13.0 in some embodiments.

In embodiments described herein, the polyethylene composition has a melt strength in cN at 190° C. from 2.0 to 6.0, from 3.0 to 5.0 in some embodiments, from 3.0 to 4.0 in some embodiments.

In embodiments described herein, the polyethylene composition has wt % of Zone 1 from CEF from 1.0 to 6.0, from 2.0 to 5.0 in some embodiments, 3.0 to 4.8 in some embodiments.

In embodiments described herein, the polyethylene composition has wt % of Zone 2 from CEF from 65.0 to 85.0, from 70.0 to 80.0 in some embodiments, from 71.0 to 80.0 in some embodiments.

In embodiments described herein, the polyethylene composition has wt % of Zone 3 from CEF from 15.0 to 30.0, from 15.0 to 27.0 in some embodiments, from 16.0 to 26.0 in some embodiments.

In embodiments described herein, the polyethylene composition has CBDI from CEF from 35.0 to 55.0, from 38.0 to 53.0 in some embodiments, from 40.0 to 52.0 in some embodiments.

In embodiments described herein, the polyethylene composition has Viscosity Ratio at 190° C. from DMS from 3.0 to 7.0, from 3.5 to 6.0 in some embodiments, from 4.5 to 5.5 in some embodiments.

In embodiments described herein, the polyethylene composition has Tan Delta at 0.1 rad/s at 190° C. from DMS from 5.0 to 15.0, from 6.0 to 13.0 in some embodiments, from 8.0 to 12.0 in some embodiments.

In embodiments described herein, the polyethylene composition has highest peak melting point (T_(m1)) from DSC in ° C. from 115.0 to 130.0, from 117.0 to 128.0 in some embodiments, from 118.0 to 125.0 in some embodiments.

In embodiments described herein, the polyethylene composition has highest peak crystallization point (T_(c1)) from DSC in ° C. from 100.0 to 120.0, from 105.0 to 115.0 in some embodiments, from 107.0 to 110.0 in some embodiments.

In embodiments described herein, the polyethylene composition has a percent crystallinity from DSC from 40.0 to 60.0, from 43.0 to 55.0 in some embodiments, from 45.0 to 50.0 in some embodiments.

In embodiments described herein, the polyethylene composition has a vinyl unsaturation of greater than 0.12 vinyls per one thousand carbon atoms (“1000 C”). All individual values and subranges from greater than 0.12 vinyls per 1000 carbon atoms are included and disclosed herein. In some embodiments, the polyethylene composition may have greater than or equal to 0.13, 0.14, 0.15, or 0.16 vinyls per 1000 carbon atoms. In other embodiments, the polyethylene composition may have vinyls per 1000 carbon atoms ranging from a lower limit of greater than 0.12, 0.13, 0.14, 0.15, 0.16, or 0.17 to an upper limit of 0.50, 0.45, 0.40, 0.35, 0.30, 0.26, 0.25, 0.24, 0.23, 0.22, 0.21, or 0.20. In further embodiments, the polyethylene composition may have greater than 0.12 to 0.50, 0.13 to 0.45, 0.14 to 0.40, 0.14 to 0.35, 0.14 to 0.30, 0.14 to 0.25, or 0.15 to 0.22 vinyls per 1000 carbon atoms.

The layer in the film comprising the polyethylene composition, in some embodiments, further comprises a low density polyethylene (LDPE). The film layer may comprise 50% or less by weight of the LDPE, based on the weight of the film layer, in some embodiments. In some embodiments, the film layer comprises from 5 to 30 wt. %, based on the total weight of polymers present in the film layer, of a LDPE. All individual values and subranges from 5 to 30 wt. % are included and disclosed herein. For example, in some embodiments, the film layer may comprise from 10 to 30 wt. %, based on the total weight of polymers present in the film layer, of a LDPE. In other embodiments, the film layer may comprise from 10 to 25 wt. %, based on the total weight of polymers present in the film layer, of a LDPE. In further, embodiments, the film layer may comprise from 10 to 20 wt. %, based on the total weight of polymers present in the film layer, of a LDPE.

In embodiments herein, the LDPE present may have a density of about 0.915-0.935 g/cm³. All individual values and subranges from 0.915-0.935 g/cm³ are included and disclosed herein. For example, in some embodiments, the LDPE has a density of 0.915-0.930 g/cm³. In other embodiments, the LDPE has a density of 0.915-0.925 g/cm³. In embodiments herein, the LDPE may have a melt index, I₂, of 0.1-20 g/10 min. All individual values and subranges from 0.1-20 g/10 min are included and disclosed herein. For example, in some embodiments, the LDPE has a melt index, I₂, of 0.5 to 20 g/10 min, 0.5 to 18 g/10 min, 0.5 to 16 g/10 min, 0.5 to 14 g/10 min, 0.5 to 12 g/10 min, 0.1 to 5 g/10 min, or 0.5 to 10 g/10 min. In other embodiments, the LDPE has a melt index, I₂, of 1 to 20 g/10 min, 1 to 18 g/10 min, 1 to 16 g/10 min, 1 to 14 g/10 min, 1 to 12 g/10 min, 0.1 to 4 g/10 min, or 1 to 10 g/10 min.

The term LDPE may also be used to refer to “high pressure ethylene polymer” or “highly branched polyethylene,” and may include branched polymers that are partly or entirely homopolymerized or copolymerized in autoclave or tubular reactors at pressures above 14,500 psi (100 MPa) with the use of free-radical initiators, such as peroxides (see for example U.S. Pat. No. 4,599,392, incorporated herein by reference). Examples of suitable LDPEs may include, but are not limited to, ethylene homopolymers, and high pressure copolymers, including ethylene interpolymerized with, for example, vinyl acetate, ethyl acrylate, butyl acrylate, acrylic acid, methacrylic acid, carbon monoxide, or combinations thereof. Exemplary LDPE resins may include resins sold by The Dow Chemical Company, such as, LDPE 722, LDPE 6401, LDPE 1321, LDPE 230N, LDPE 586A, and LDPE 6211, as well as EB873/72 LDPE resin commercially available from Braskem.

In some embodiments, minor amounts of other polymers can also be included in the film layer comprising the polyethylene composition and the LDPE. Examples of such other polymers include, without limitation, polyethylene (homopolymers or copolymers), polypropylene (homopolymers or copolymers), cyclic olefin copolymers, and others.

It should be understood that this layer, as well as any other layer when the film is a multilayer film, can further comprise one or more additives as known to those of skill in the art such as, for example, antioxidants, ultraviolet light stabilizers, thermal stabilizers, slip agents, antiblock, pigments or colorants, processing aids, crosslinking catalysts, flame retardants, fillers and foaming agents.

As previously indicated, in some embodiments, the film can be a multilayer film. In such embodiments, any additional layers would be in adhering contact with a top facial surface or a bottom facial surface of the layer with the polyethylene composition, or another intermediate layer. For example, a multilayer film can further comprise other layers typically included in multilayer films depending on the application including, for example, printed layers, sealant layers, barrier layers, tie layers, other polyethylene layers, etc.

Films of the present invention can be formed using techniques known to those of skill in the art based on the teachings herein. For example, such films can be extruded (or coextruded in the case of multilayer films) as blown films or cast films using techniques known to those of skill in the art based on the teachings herein.

Films of the present invention can be used to form an article. Films of the present invention might be particularly useful in articles that require a film with high dart, puncture and/or tear resistance properties. Such articles can be formed from any of the films described herein. Examples of such articles can include flexible packages such as pouches, stand-up pouches, and pre-made packages or pouches. In some embodiments, multilayer films of the present invention can be used for food packages. Examples of food that can be included in such packages include meats, cheeses, cereal, nuts, juices, sauces, and others. Such packages can be formed using techniques known to those of skill in the art based on the teachings herein and based on the particular use for the package (e.g., type of food, amount of food, etc.).

Flexible packages utilizing films of the present invention can advantageously be formed with heat seal packaging equipment utilizing continuously heated seal bars, in some embodiments. Examples of such packaging equipment utilizing continuously heated seal bars include horizontal form-fill-seal machines and vertical form-fill-seal machines. Examples of packages that can be formed from such equipment include stand-up pouches, 4-corner packages (pillow pouches), fin seal packages and others.

Test Methods Density

Samples for density measurements were prepared according to ASTM D 4703-10 Annex A1 Procedure C. Approximately 7 g of sample was placed in a “2″×2″×135 mil thick” mold, and this was pressed at 374° F. (190° C.) for six minutes at 3,000 lbf (0.0133 MN). Then the pressure was increased to 30,000 lbf (0.133 MN) for four minutes. This was followed by cooling at 15° C. per minute, at 30,000 lbf (0.133 MN), to approximately a temperature of 40° C. The “2″×2″×135 mil” polymer sample (plaque) was then removed from the mold, and three samples were cut from the plaque with a ½″×1″ die cutter. Density measurements were made within one hour of sample pressing, using ASTM D792-08, Method B. Density was reported as an average of three measurements.

Melt Index

Melt index (I₂) can be measured in accordance with ASTM D-1238, Procedure B (condition 190° C./2.16 kg). Melt index (I₁₀) can be measured in accordance with ASTM D-1238, Procedure B (condition 190° C./10.0 kg).

Gel Permeation Chromatography (GPC)

The chromatographic system consisted of a PolymerChar GPC-IR (Valencia, Spain) high temperature GPC chromatograph equipped with an internal IR5 detector. The autosampler oven compartment was set at 160° Celsius and the column compartment was set at 150° Celsius. The columns used were 3 Agilent “Mixed B” 30 cm 10-micron linear mixed-bed columns and a 10-μm pre-column. The chromatographic solvent used was 1,2,4 trichlorobenzene and contained 200 ppm of butylated hydroxytoluene (BHT). The solvent source was nitrogen sparged. The injection volume used was 200 microliters and the flow rate was 1.0 milliliters/minute.

Calibration of the GPC column set was performed with 21 narrow molecular weight distribution polystyrene standards with molecular weights ranging from 580 to 8,400,000 and were arranged in 6 “cocktail” mixtures with at least a decade of separation between individual molecular weights. The standards were purchased from Agilent Technologies. The polystyrene standards were prepared at 0.025 grams in 50 milliliters of solvent for molecular weights equal to or greater than 1,000,000, and 0.05 grams in 50 milliliters of solvent for molecular weights less than 1,000,000. The polystyrene standards were dissolved at 80 degrees Celsius with gentle agitation for 30 minutes. The polystyrene standard peak molecular weights were converted to polyethylene molecular weights using Equation 1 (as described in Williams and Ward, J. Polym. Sci., Polym. Let., 6, 621 (1968)):

M _(polyethylene) =A×(M _(polystyrene))^(B)  (EQ1)

where M is the molecular weight, A has a value of 0.4315 and B is equal to 1.0.

A fifth order polynomial was used to fit the respective polyethylene-equivalent calibration points. A small adjustment to A (from approximately 0.415 to 0.44) was made to correct for column resolution and band-broadening effects such that NIST standard NBS 1475 is obtained at 52,000 g/mol Mw.

The total plate count of the GPC column set was performed with Eicosane (prepared at 0.04 g in 50 milliliters of TCB and dissolved for 20 minutes with gentle agitation.) The plate count (Equation 2) and symmetry (Equation 3) was measured on a 200 microliter injection according to the following equations:

$\begin{matrix} {{Plate}\mspace{14mu}{Count}{= {{5.5}4*\left( \frac{{RV}_{{Peak}\mspace{14mu}{Max}}}{{Peak}\mspace{14mu}{Width}\mspace{14mu}{at}\frac{1}{2}{height}} \right)^{2}}}} & ({EQ2}) \end{matrix}$

where RV is the retention volume in milliliters, the peak width is in milliliters, the peak max is the maximum height of the peak, and ½ height is ½ height of the peak maximum.

$\begin{matrix} {{Symmetry} = \frac{\left( {{{Rear}\mspace{14mu}{Peak}\mspace{14mu}{RV}_{{one}\mspace{14mu}{tenth}\mspace{14mu}{height}}} - {RV}_{{Peak}\mspace{14mu}\max}} \right)}{\left( {{RV}_{{Peak}\mspace{14mu}\max} - {{Front}\mspace{14mu}{Peak}\mspace{14mu}{RV}_{{one}\mspace{14mu}{tenth}\mspace{14mu}{height}}}} \right)}} & ({EQ3}) \end{matrix}$

where RV is the retention volume in milliliters and the peak width is in milliliters, peak max is the maximum position of the peak, one tenth height is 1/10 height of the peak maximum, rear peak refers to the peak tail at later retention volumes than the peak max, and front peak refers to the peak front at earlier retention volumes than the peak max. The plate count for the chromatographic system should be greater than 24,000 and symmetry should be between 0.98 and 1.22.

Samples were prepared in a semi-automatic manner with the PolymerChar “Instrument Control” Software, wherein the samples were weight-targeted at 2 mg/ml, and the solvent (contained 200 ppm BHT) was added to a pre nitrogen-sparged septa-capped vial, via the PolymerChar high temperature autosampler. The samples were dissolved for 2 hours at 160° Celsius under “low speed” shaking.

The calculations of M_(n), M_(w), and M_(z) were based on GPC results using the internal IR5 detector (measurement channel) of the PolymerChar GPC-IR chromatograph according to Equations 4-6, using PolymerChar GPCOne™ software, the baseline-subtracted IR chromatogram at each equally-spaced data collection point (i), and the polyethylene equivalent molecular weight obtained from the narrow standard calibration curve for the point (i) from Equation 1.

$\begin{matrix} {M_{n} = \frac{\sum\limits^{i}\;{IR}_{i}}{\sum\limits^{i}\;\left( {{IR}_{i}/M_{{polyethylene}_{\; i}}^{\;}} \right)}} & ({EQ4}) \\ {M_{w} = \frac{\sum\limits^{i}\;\left( {{IR}_{i}*M_{{polyethylene}_{\; i}}} \right)}{\sum\limits^{i}{IR}_{i}}} & ({EQ5}) \\ {M_{z} = \frac{\sum\limits^{i}\;\left( {{IR}_{i}*M_{{polyethylene}_{\; i}}^{2}} \right)}{\sum\limits^{i}\;\left( {{IR}_{i}*M_{{polyethylene}_{\; i}}^{\;}} \right)}} & ({EQ6}) \end{matrix}$

In order to monitor the deviations over time, a flowrate marker (decane) was introduced into each sample via a micropump controlled with the PolymerChar GPC-IR system. This flowrate marker was used to linearly correct the flowrate for each sample by alignment of the respective decane peak within the sample to that of the decane peak within the narrow standards calibration. Any changes in the time of the decane marker peak are then assumed to be related to a linear shift in both flowrate and chromatographic slope. To facilitate the highest accuracy of a RV measurement of the flow marker peak, a least-squares fitting routine is used to fit the peak of the flow marker concentration chromatogram to a quadratic equation. The first derivative of the quadratic equation is then used to solve for the true peak position. After calibrating the system based on a flow marker peak, the effective flowrate (as a measurement of the calibration slope) is calculated as Equation 7. Processing of the flow marker peak was done via the PolymerChar GPCOne™ Software.

$\begin{matrix} {{Flowrate_{effective}} = {Flowrate_{nominal} \times \frac{FlowMarker_{Calibration}}{FlowMarker_{Observed}}}} & ({EQ7}) \end{matrix}$

Neutron Activation Method for Metals

Two sets of duplicate samples were prepared by transferring approximately 3.5 grams of the pellets into pre-cleaned 2 dram polyethylene vials. Standards were prepared for each metal tested from their NIST traceable standard solutions (Certi. pure from SPEX) into 2-dram polyethylene vials. They were diluted using milli-Q pure water to 6 ml and the vials were heat-sealed. The samples and standards were then analyzed for these elements, using a Mark I TRIGA nuclear reactor. The reactions and experimental conditions used for these elements are summarized in the table below. The samples were transferred to un-irradiated vials before doing the gamma-spectroscopy. The elemental concentrations were calculated using CANBERRA software and standard comparative technique. Table 1 provides measurement parameters for metals determination.

TABLE 1 Reactions and experimental conditions used for elements during the neutron activation method Elements Nuclear reaction Isotope Half life Reactor Power Al ²⁷Al(n, γ)²⁸Al ²⁸Al 2.24 m 250 kW Cl ³⁷Cl(n, γ)³⁸Cl ³⁸Cl 37.2 m 250 kW Cr ⁵⁰Cr(n, γ)⁵¹Cr ⁵¹Cr 27.7 d 250 kW Hf ¹⁸⁰Hf(n, γ)¹⁸¹Hf ¹⁸¹Hf 42.4 d 250 kW Mg ²⁶Mg(n, γ)²⁷Mg ²⁷Mg 9.46 m 250 kW Mo ⁹⁸Mo(n, γ)⁹⁹Mo ⁹⁹Mo 66.0 h 250 kW Nb ⁹³Nb(n, γ)^(94m)Nb ^(94m)Nb 6.26 m 250 kW Ta ¹⁸¹Ta(n, γ)¹⁸²Ta ¹⁸²Ta 114.4 d 250 kW Ti ⁵⁰Ti(n, γ)⁵¹Ti ⁵¹Ti 5.76 m 250 kW W ¹⁸⁶W(n, γ)¹⁸⁷W ¹⁸⁷W 23.7 h 250 kW V ⁵¹V(n, γ)⁵²V ⁵²V 3.75 m 250 kW Zr ⁹⁶Zr(n, γ)⁹⁷Zr ⁹⁷Zr 16.91 h 250 kW Waiting Counting Gamma Energy, Elements Irradiation Time Time Time keV Al  2 m 4 m 4.5 min 1778.5 Cl  2 m 4 m 4.5 min 1642.5, 2166.5 Cr 90 m 5 h 1.6 h  320 Hf 90 m 5 h 1.6 h 133, 482 Mg  2 m 4 m 4.5 min 843.8, 1014 Mo 90 m 5 h 1.6 h 181, 739.7, 141 Nb  2 m 4 m 4.5 min  871 Ta 90 m 5 h 1.6 h 1121, 1222 Ti  2 m 4 m 4.5 min  320 W 90 m 5 h 1.6 h 135, 481 V  2 m 4 m 4.5 min 1434 Zr 90 m 5 h 1.6 h  743.4 Differential Scanning calorimetry (DSC)

DSC was used to measure the melting and crystallization behavior of a polymer over a wide range of temperatures. For example, the TA Instruments Q1000 DSC, equipped with an RCS (refrigerated cooling system) and an autosampler was used to perform this analysis. During testing, a nitrogen purge gas flow of 50 ml/min was used. Each sample was melt pressed into a thin film at about 175° C.; the melted sample was then air-cooled to room temperature (approx. 25° C.). The film sample was formed by pressing a “0.1 to 0.2 gram” sample at 175° C. at 1,500 psi, and 30 seconds, to form a “0.1 to 0.2 mil thick” film. A 3-10 mg, 6 mm diameter specimen was extracted from the cooled polymer, weighed, placed in a light aluminum pan (ca 50 mg), and crimped shut. Analysis was then performed to determine its thermal properties.

The thermal behavior of the sample was determined by ramping the sample temperature up and down to create a heat flow versus temperature profile. First, the sample was rapidly heated to 180° C., and held isothermal for five minutes, in order to remove its thermal history. Next, the sample was cooled to −40° C., at a 10° C./minute cooling rate, and held isothermal at −40° C. for five minutes. The sample was then heated to 150° C. (this is the “second heat” ramp) at a 10° C./minute heating rate. The cooling and second heating curves were recorded. The cool curve was analyzed by setting baseline endpoints from the beginning of crystallization to −20° C. The heat curve was analyzed by setting baseline endpoints from −20° C. to the end of melt. The values determined were peak melting temperature (T_(m)), peak crystallization temperature (TO, heat of fusion (H_(f)) (in Joules per gram), and the calculated % crystallinity for polyethylene samples using: % Crystallinity=((H_(f))/(292 J/g))×100. The heat of fusion (H_(f)) and the peak melting temperature were reported from the second heat curve. Peak crystallization temperature is determined from the cooling curve.

Melt Strength

Melt strength was measured at 190° C. using a Göettfert Rheotens 71.97 (Göettfert Inc.; Rock Hill, S.C.), melt fed with a Göettfert Rheotester 2000 capillary rheometer equipped with a flat entrance angle (180 degrees) of length of 30 mm and diameter of 2.0 mm. The pellets (20-30 gram pellets) were fed into the barrel (length=300 mm, diameter=12 mm), compressed and allowed to melt for 10 minutes before being extruded at a constant piston speed of 0.265 mm/s, which corresponds to a wall shear rate of 38.2 s⁻¹ at the given die diameter. The extrudate passed through the wheels of the Rheotens located 100 mm below the die exit and was pulled by the wheels downward at an acceleration rate of 2.4 mm/s². The force (in cN) exerted on the wheels was recorded as a function of the velocity of the wheels (in mm/s). Melt strength is reported as the plateau force (cN) before the strand broke.

Dynamic Mechanical Spectroscopy (DMS)

Resins were compression-molded into “3 mm thick×1 inch diameter” circular plaques at 350° F., for five minutes, under 1500 psi pressure, in air. The sample was then taken out of the press, and placed on a counter to cool.

A constant temperature frequency sweep was performed using a TA Instruments “Advanced Rheometric Expansion System (ARES),” equipped with 25 mm (diameter) parallel plates, under a nitrogen purge. The sample was placed on the plate, and allowed to melt for five minutes at 190° C. The plates were then closed to a gap of “2 mm,” the sample trimmed (extra sample that extends beyond the circumference of the “25 mm diameter” plate was removed), and then the test was started. The method had an additional five minute delay built in, to allow for temperature equilibrium. The experiments were performed at 190° C. over a frequency range of 0.1 to 100 rad/s. The shear strain amplitude was constant at 10%. The complex viscosity η*, tan (δ) or tan delta, viscosity at 0.1 rad/s (V0.1), the viscosity at 100 rad/s (V100), and the viscosity ratio (V0.1/V100) were calculated from these data.

Crystallization Elution Fractionation (CEF) Method

The Crystallization Elution Fractionation (CEF) technology is conducted according to Monrabal et al, Macromol. Symp. 257, 71-79 (2007). The CEF instrument is equipped with an IR-4 or IR-5 detector (such as that sold commercially from PolymerChar, Spain) and a two angle light scattering detector Model 2040 (such as those sold commercially from Precision Detectors). A 10 micron guard column of 50 mm×4.6 mm (such as that sold commercially from PolymerLabs) is installed before the IR-4 or IR-5 detector in the detector oven. Ortho-dichlorobenzene (ODCB, 99% anhydrous grade) and 2,5-di-tert-butyl-4-methylphenol (BHT) (such as commercially available from Sigma-Aldrich) are obtained. Silica gel 40 (particle size 0.2-0.5 mm) (such as commercially available from EMD Chemicals) is also obtained. The silica gel is dried in a vacuum oven at 160° C. for at least two hours before use. ODCB is sparged with dried nitrogen (N₂) for one hour before use. Dried nitrogen is obtained by passing nitrogen at <90 psig over CaCO₃ and 5 Å molecular sieves. ODCB is further dried by adding five grams of the dried silica to two liters of ODCB or by pumping through a column or columns packed with dried silica between 0.1 ml/min to 1.0 ml/min. Eight hundred milligrams of BHT are added to two liters of ODCB if no inert gas such as N₂ is used in purging the sample vial. Dried ODCB with or without BHT is hereinafter referred to as “ODCB-m.” A sample solution is prepared by, using the autosampler, dissolving a polymer sample in ODCB-m at 4 mg/ml under shaking at 160° C. for 2 hours. 300 μL of the sample solution is injected into the column. The temperature profile of CEF is: crystallization at 3° C./min from 110° C. to 30° C., thermal equilibrium at 30° C. for 5 minutes (including Soluble Fraction Elution Time being set as 2 minutes), and elution at 3° C./min from 30° C. to 140° C. The flow rate during crystallization is 0.052 ml/min. The flow rate during elution is 0.50 ml/min. The IR-4 or IR-5 signal data is collected at one data point/second.

The CEF column is packed with glass beads at 125 μm±6% (such as those commercially available with acid wash from MO-SCI Specialty Products) with ⅛ inch stainless tubing according to U.S. Pat. No. 8,372,931. The internal liquid volume of the CEF column is between 2.1 ml and 2.3 ml. Temperature calibration is performed by using a mixture of NIST Standard Reference Material linear polyethylene 1475a (1.0 mg/ml) and Eicosane (2 mg/ml) in ODCB-m. The calibration consists of four steps: (1) calculating the delay volume defined as the temperature offset between the measured peak elution temperature of Eicosane minus 30.00° C.; (2) subtracting the temperature offset of the elution temperature from the CEF raw temperature data. It is noted that this temperature offset is a function of experimental conditions, such as elution temperature, elution flow rate, etc.; (3) creating a linear calibration line transforming the elution temperature across a range of 30.00° C. and 140.00° C. such that NIST linear polyethylene 1475a has a peak temperature at 101.00° C., and Eicosane has a peak temperature of 30.00° C., (4) for the soluble fraction measured isothermally at 30° C., the elution temperature is extrapolated linearly by using the elution heating rate of 3° C./min. The reported elution peak temperatures are obtained such that the observed comonomer content calibration curve agrees with those previously reported in U.S. Pat. No. 8,372,931.

The CEF chromatogram is divided into zones, the elution temperature range of each zone is specified.

Comonomer Distribution Breadth Index (CDBI)

The CDBI is calculated using the methodology described in WO/93/03093 from data obtained from CEF. CDBI is defined as the weight percent of the polymer molecules having a comonomer content within 50 percent of the median total molar comonomer content. It represents a comparison of the comonomer distribution in the polymer to the comonomer distribution expected for a Bernoullian distribution.

CEF is used to measure the short chain branching distribution (SCBD) of the polyolefin. A CEF molar comonomer content calibration is performed using 24 reference materials (e.g., polyethylene octene random copolymer and ethylene butene copolymer) with a narrow SCBD having a comonomer mole fraction ranging from 0 to 0.108 and a Mw from 28,400 to 174,000 g/mole. The ln (mole fraction of ethylene), which is the ln (comonomer mole fraction), versus 1/T (K) is obtained, where T is the elution temperature in Kelvin of each reference material. The comonomer distribution of the reference materials is determined using 13C NMR analysis in accordance with techniques described, for example, in U.S. Pat. No. 5,292,845 (Kawasaki, et al.) and by J. C. Randall in Rev. Macromol. Chem. Phys., C29, 201-317.

Nuclear Magnetic Resonance (¹H NMR)

The samples were prepared by adding approximately 130 mg of sample to “3.25 g of 50/50, by weight, tetrachlorethane-d₂/perchloroethylene (TCE-d₂)” with 0.001 M Cr(AcAc)₃ in a NORELL 1001-7, 10 mm NMR tube. The samples were purged by bubbling N₂ through the solvent, via a pipette inserted into the tube, for approximately five minutes, to prevent oxidation. Each tube was capped, sealed with TEFLON tape, and then soaked at room temperature, overnight, to facilitate sample dissolution. The samples were heated and vortexed at 115° C. to ensure homogeneity.

The ¹H NMR was performed on a Bruker AVANCE 400 MHz spectrometer, equipped with a Bruker Dual DUL high-temperature CryoProbe, and a sample temperature of 120° C. Two experiments were run to obtain spectra, a control spectrum to quantitate the total polymer protons, and a double presaturation experiment, which suppressed the intense polymer backbone peaks, and enabled high sensitivity spectra for quantitation of the end-groups. The control was run with ZG pulse, 16 scans, AQ 1.64 s, D1 14 s. The double presaturation experiment was run with a modified pulse sequence, 100 scans, AQ 1.64 s, presaturation delay 1 s, relaxation delay 13 s.

The signal from residual ¹H in TCE-d₂ (at 6.0 ppm) was integrated, and set to a value of 100, and the integral from 3 to −0.5 ppm was used as the signal from the whole polymer in the control experiment. For the presaturation experiment, the TCE signal was also set to 100, and the corresponding integrals for unsaturation (vinylene at about 5.25 to 5.60 ppm, trisubstituted at about 5.16 to 5.25 ppm, vinyl at about 4.95 to 5.15 ppm, and vinylidene at about 4.70 to 4.90 ppm) were obtained.

In the presaturation experiment spectrum, the regions for cis- and trans-vinylene, trisubstituted, vinyl, and vinylidene were integrated. The integral of the whole polymer from the control experiment was divided by two to obtain a value representing X thousands of carbons (i.e., if the polymer integral=28000, this represents 14,000 carbons, and X=14).

The unsaturated group integrals, divided by the corresponding number of protons contributing to that integral, represent the moles of each type of unsaturation per X thousand carbons. Dividing the moles of each type of unsaturation by X, then gives moles unsaturated groups per 1000 moles of carbons.

Film Property Test Methods Dart Drop Test

The film Dart Drop test determines the energy that causes a plastic film to fail, under specified conditions of impact by a free falling dart. The test result is the Dart Impact which reflects the energy, expressed in terms of the weight of the missile falling from a specified height, which would result in the failure of 50% of the specimens tested.

After the film was produced on the blown film line, it was conditioned for at least 40 hours at 23° C. (+/−2° C.) and 50% R.H (+/−5), as per ASTM standards. Standard testing conditions are 23° C. (+/−2° C.) and 50% R.H (+/−5), as per ASTM standards.

The test result was reported as either by Method A, which uses a 1.5″ diameter dart head and 26″ drop height, or by Method B, which uses a 2″ diameter dart head and 60″ drop height. The sample thickness was measured at the sample center, and the sample was then clamped by an annular specimen holder with an inside diameter of 5 inches. The dart was loaded above the center of the sample, and released by either a pneumatic or electromagnetic mechanism.

Testing was carried out according to the ‘staircase’ method. If the sample failed, a new sample was tested with the weight of the dart reduced by a known and fixed amount. If the sample did not fail, a new sample was tested with the weight of the dart increased by a known amount. After 20 specimens had been tested, the number of failures was determined. If this number was 10, then the test is complete. If the number was less than 10, then the testing continued, until 10 failures had been recorded. If the number was greater than 10, testing was continued, until the total of non-failures was 10. The Dart Drop Strength was determined from these data, as per ASTM D1709, and expressed in grams, as either the Dart Drop Impact of Type A or Type B. In some cases, the sample Dart Drop Impact strength may lie between A and B. In these cases, it is not possible to obtain a quantitative dart value.

Puncture

Puncture is measured using ASTM D5748, except that the probe used is 0.5″ in diameter and is stainless steel. Speed=250 mm/min.

Elmendorf Tear

Elmendorf tear test data is measured on all films in accordance with ASTM D1922-09. All samples are tested in the machine direction (MD) and the cross-direction (CD). 15 specimens per each sample are tested and the average value is recorded.

EXAMPLES

A multi-metal catalyst is prepared (Catalyst 1). Catalyst 1 is then used to prepare an inventive polyethylene composition in a solution polymerization. Subsequently, the inventive and comparative polyethylene compositions are used to prepare inventive and comparative blown films, respectively. Testing is carried out on both the polyethylene compositions and the blown films.

General Description of Preparation of Catalysts

The catalyst compositions may be prepared beginning first with preparation of a conditioned magnesium halide based support. Preparation of a conditioned magnesium halide based support begins with selecting an organomagnesium compound or a complex including an organomagnesium compound. Such compound or complex is desirably soluble in an inert hydrocarbon diluent. In one embodiment, the concentrations of components are such that when the active halide, such as a metallic or non-metallic halide, and the magnesium complex are combined, the resultant slurry is from about 0.005 to about 0.3 molar (moles/liter) with respect to magnesium. Examples of suitable inert organic diluents include liquefied ethane, propane, isobutane, n-butane, n-hexane, the various isomeric hexanes, isooctane, paraffinic mixtures of alkanes having from 5 to 10 carbon atoms, cyclohexane, methylcyclopentane, dimethylcyclohexane, dodecane, industrial solvents composed of saturated or aromatic hydrocarbons such as kerosene, naphthas, and combinations thereof, especially when freed of any olefin compounds and other impurities, and especially those having boiling points in the range from about −50° C. to about 200° C. Also included as suitable inert diluents are ethylbenzene, cumene, decalin and combinations thereof.

Suitable organomagnesium compounds and complexes may include, for example, magnesium C2-C8 alkyls and aryls, magnesium alkoxides and aryloxides, carboxylated magnesium alkoxides, and carboxylated magnesium aryloxides. Preferred sources of magnesium moieties may include the magnesium C2-C8 alkyls and C1-C4 alkoxides. Such organomagnesium compound or complex may be reacted with a metallic or non-metallic halide source, such as a chloride, bromide, iodide, or fluoride, in order to make a magnesium halide compound under suitable conditions. Such conditions may include a temperature ranging from −25° C. to 100° C., or alternatively, 0° C. to 50° C.; a time ranging from 1 to 12 hours, or alternatively, from 4 to 6 hours; or both. The result is a magnesium halide-based support.

The magnesium halide support is then reacted with a selected conditioning compound containing an element selected from the group consisting of boron, aluminum, gallium, indium and tellurium, under conditions suitable to form a conditioned magnesium halide support. This compound and the magnesium halide support are then brought into contact under conditions sufficient to result in a conditioned magnesium halide support. Such conditions may include a temperature ranging from 0° C. to 50° C., or alternatively, from 25° C. to 35° C.; a time ranging from 4 to 24 hours, or alternatively, from 6 to 12 hours; or both. Without wishing to be bound by any theory of mechanism, it is suggested that this aging serves to facilitate or enhance adsorption of additional metals onto the support.

Once the conditioned support is prepared and suitably aged, it is brought into contact with a titanium compound. In certain preferred embodiments, titanium halides or alkoxides, or combinations thereof, may be selected. Conditions may include a temperature within the range from 0° C. to 50° C., or alternatively, from 25° C. to 35° C.; a time from 3 hours to 24 hours, or alternatively, from 6 hours to 12 hours; or both. The result of this step is adsorption of at least a portion of the titanium compound onto the conditioned magnesium halide support.

Additional Steps in Preparing Multi-Metal Catalyst Used to Make the Inventive Polyethylene Composition

For those catalysts used to make the inventive polyethylene composition, i.e. multi-metal catalysts herein, two additional metals, referred to herein as “the second metal” and “the third metal” for convenience, will also be adsorbed onto the magnesium based support, The “second metal” and the “third metal” are independently selected from zirconium (Zr), hafnium (Hf), vanadium (V), niobium (Nb), tantalum (Ta), chromium (Cr), molybdenum (Mo), and tungsten (W). These metals may be incorporated in any of a variety of ways known to those skilled in the art, but generally contact between the conditioned magnesium based halide support including titanium and the selected second and third metals, in, e.g., liquid phase such as an appropriate hydrocarbon solvent, will be suitable to ensure deposition of the additional metals to form what may now be referred to as the “procatalyst,” which is a multi-metallic procatalyst.

In certain embodiments, the multi-metal procatalyst exhibits a molar ratio of the magnesium to a combination of the titanium and the second and third metals that ranges from 30:1 to 5:1; under conditions sufficient to form a multi-metallic procatalyst. Thus, the overall molar ratio of magnesium to titanium ranges from 8:1 to 80:1.

Once the procatalyst has been formed, it may be used to form a final catalyst by combining it with a cocatalyst consisting of at least one organometallic compound such as an alkyl or haloalkyl of aluminum, an alkylaluminum halide, a Grignard reagent, an alkali metal aluminum hydride, an alkali metal borohydride, an alkali metal hydride, an alkaline earth metal hydride, or the like. The formation of the final catalyst from the reaction of the procatalyst and the organometallic cocatalyst may be carried out in situ, or just prior to entering the polymerization reactor. Thus, the combination of the cocatalyst and the procatalyst may occur under a wide variety of conditions. Such conditions may include, for example, contacting them under an inert atmosphere such as nitrogen, argon or other inert gas at temperatures in the range from 0° C. to 250° C., or alternatively, from 15° C. to 200° C. In the preparation of the catalytic reaction product, it is not necessary to separate hydrocarbon soluble components from hydrocarbon insoluble components. Time for contact between the procatalyst and cocatalyst may range, for example, from 0 to 240 seconds, or alternatively, from 5 to 120 seconds. Various combinations of these conditions may be employed.

Catalyst I Preparation

To approximately 109 kg of 0.20 M MgCl₂ slurry was added 7.76 kg of (C₂H₅)AlCl₂ (EADC) solution (15 wt. % in heptanes), followed by agitation for 8 hours. A mixture of TiCl₄/VOCl₃ (85 mL and 146 mL, respectively) was then added, followed by a solution of Zr(TMHD)₄ (Zirconium tetrakis(2,2,6,6-tetramethyl-3,5-heptanedionate) (0.320 kg of a 0.30 M solution in Isopar E). These two additions were performed sequentially within 1 hour of each other. The resulting catalyst premix was aged with agitation for an additional 8 h prior to use.

Catalyst 1 prepared hereinabove is then used to prepare Polyethylene Compositions as described below.

Production of Inventive Polyethylene Compositions

The polyethylene resins are produced via a solution polymerization according to the following exemplary process. All raw materials (monomer and comonomer) and the process solvent (a narrow boiling range high-purity isoparaffinic solvent, Isopar-E) are purified with molecular sieves before introduction into the reaction environment. Hydrogen is supplied in pressurized cylinders as a high purity grade and is not further purified. The reactor monomer feed stream is pressurized via a mechanical compressor to above reaction pressure. The fresh comonomer is pressurized via a pump and injected into the solvent feed stream to the reactor. The solvent and comonomer feed is then pressurized via a pump to above reaction pressure. The individual catalyst components are manually batch diluted to specified component concentrations with purified solvent and pressured to above reaction pressure. All reaction feed flows are measured with mass flow meters and independently controlled with computer automated valve control systems.

The continuous solution polymerization reactor consists of a liquid full, non-adiabatic, isothermal, circulating, loop reactor which mimics a continuously stirred tank reactor (CSTR) with heat removal. Independent control of all fresh solvent, monomer, comonomer, hydrogen, and catalyst component feeds is possible. The total fresh feed stream to the reactor (solvent, monomer, comonomer, and hydrogen) is temperature controlled by passing the feed stream through a heat exchanger. The total fresh feed to the polymerization reactor is injected into the reactor at two locations with approximately equal reactor volumes between each injection location. The fresh feed is controlled with each injector receiving half of the total fresh feed mass flow. The catalyst components are injected into the polymerization reactor through a specially designed injection stinger and are combined into one mixed catalyst/cocatalyst feed stream prior to injection into the reactor. The primary catalyst component feed is computer controlled to maintain the reactor monomer concentration at a specified target. The cocatalyst component is fed based on calculated specified molar ratio to the primary catalyst component. Immediately following each fresh injection location (either feed or catalyst), the feed streams are mixed with the circulating polymerization reactor contents with static mixing elements. The contents of the reactor are continuously circulated through heat exchangers responsible for removing much of the heat of reaction and with the temperature of the coolant side responsible for maintaining an isothermal reaction environment at the specified temperature. Circulation around the reactor loop is provided by a positive displacement pump.

The final reactor effluent enters a zone where it is deactivated with the addition of and reaction with water. At this same reactor exit location other additives may also be added (such as an acid scavenging agent and anti-oxidants). The stream then goes through a static mixer to disperse the post reactor additive components.

Following catalyst deactivation and additive addition, the reactor effluent enters a devolatization system where the polymer is removed from the non-polymer stream. The isolated polymer melt is pelletized and collected. The non-polymer stream passes through various pieces of equipment which separate most of the ethylene which is removed from the system. Most of the solvent and unreacted comonomer is recycled back to the reactor after passing through a purification system. A small amount of solvent and comonomer is purged from the process.

Table 2 summarizes the polymerization conditions for the Inventive Polyethylene Compositions (IE). Additives used in these polymerizations are 1250 ppm calcium stearate, 1000 ppm IRGAFOS 168 (which is tris (2,4 di-tert-butylphenyl) phosphite), 250 ppm IRGANOX 1076 (which is octadecyl-3-(3,5-di-tert-butyl-4-hydroxyphenyl)propionate)), 200 ppm IRGANOX 1010 (which is Pentaerythritol Tetrakis (3-(3,5-di-tert-butyl-4-hydroxyphenyl)propionate)), and 300 ppm Hydrotalcite, as well as conventional slip, antiblock and optical brighteners additives. IRGAFOS 168, IRGANOX 1010 and IRGANOX 1076 are commercially available from BASF.

TABLE 2 Polymerization Conditions Sample IE 1 IE 2 IE 3 Reactor Configuration Type Single Single Single Comonomer type Type 1-octene 1-hexene 1-octene Reactor Feed Solvent / Ethylene Mass Flow Ratio g/g 3.4 4.1 3.5 Reactor Feed Comonomer / Ethylene Mass Flow g/g 0.63 0.45 0.48 Ratio Reactor Feed Hydrogen / Ethylene Mass Flow Ratio g/g 1.0E−04 4.0E−05 5.2E−05 Reactor Temperature ° C. 175 190 192 Reactor Pressure barg 50 50 50 Reactor Ethylene Conversion % 92.0 92.0 92.4 Reactor Catalyst Type Type Catalyst 1 Catalyst 1 Catalyst 1 Reactor Co-Catalyst Type Type TEA* TEA* TEA* Reactor Co-Catalyst to Catalyst Molar Ratio (Al to Ratio 12.0 10.0 11.0 Ti ratio) Reactor Residence Time Min 6.4 6.1 7.0 *TEA is tri-ethyl-aluminum.

A variety of properties set forth in the below Tables are measured for IE1-IE3 as well as for three linear low density polyethylenes that are also used to make the films. LLDPE1 is DOWLEX™ TG 2085B linear low density polyethylene commercially available from The Dow Chemical Company. LLDPE2 is DOWLEX™ 2685G linear low density polyethylene commercially available from The Dow Chemical Company. LLDPE3 is Flexus 9211 metallocene-catalyzed linear low density polyethylene commercially available from Braskem.

TABLE 3 Comonomer, Measured Melt Index, and Density Data 12, g/10 I10/I2, Density Sample Comonomer min g/10 min (g/cc) IE1 Octene 0.92 7.32 0.9200 IE2 Hexene 0.74 7.26 0.9185 IE3 Octene 1.00 7.37 0.9208 LLDPE1 Octene 0.94 8.05 0.9197 LLDPE2 Hexene 0.72 8.27 0.9194 LLDPE3 Hexene 1.01 5.75 0.9182

TABLE 4 Conventional GPC Data Mn Mw Mz Sample (g/mol) (g/mol) (g/mol) Mw/Mn Mz/Mw Mz/Mn IE1 32,416 119,968 396,896 3.70 3.31 12.24 IE2 35,375 129,224 430,529 3.65 3.33 12.17 IE3 32,624 122,700 405,632 3.76 3.31 12.43 LLDPE1 30,815 122,947 395,947 3.99 3.22 12.85 LLDPE2 31,000 131,902 442,826 4.25 3.36 14.28 LLDPE3 43,501 107,777 194,006 2.48 1.80 4.46

TABLE 5 Melt Strength Data Velocity at Melt Break Strength Sample (mm/s) (cN) IE1 271 3.3 IE2 162 3.5 IE3 268 3.5 LLDPE1 277 3.5 LLDPE2 264 4.1 LLDPE3 259 2.5

TABLE 6 CEF and CDBI Data Peak Temperature Range of Each Peak Temperature Zone (° C.) (° C.) Wt % of Each Zone Sample Zone 1 Zone 2 Zone 3 Zone 1 Zone 2 Zone 3 Zone 1 Zone 2 Zone 3 CDBI IE1 25.0 to 34.5 34.6 to 94.1 94.2 to 120.0 28.5 85.0 98.9 4.4 75.6 20.1 45.7 IE2 25.0 to 34.5 34.6 to 93.9 94.0 to 120.0 28.5 84.9 98.5 4.4 78.8 16.8 50.2 IE3 25.0 to 34.5 34.6 to 93.9 94.0 to 120.0 28.5 85.1 99.0 3.4 72.3 24.3 41.9 LLDPE1 25.1 to 32.0 32.0 to 92.5 92.6 to 120.0 28.4 83.2 98.7 5.2 69.3 25.6 40.6 LLDPE2 25.1 to 32.0 32.1 to 92.4  92.5to 120.0 28.5 82.6 97.8 6.0 76.7 17.3 52.0 LLDPE3 25.0 to 33.6  33.7 to 120.0 NA 28.5 84.5 NA 0.7 99.3 NA 61.6 NA = Not Applicable

TABLE 7 DMS Rheology Data (at 190° C.) Viscosity (Pa-s) at 190 C. Viscosity Tan Delta Sample 0.1 rad/s 1 rad/s 10 rad/s 100 rad/s Ratio 0.1 rad/s IE1 8,913 7,065 4,368 1,801 4.95 8.66 IE2 10,369 8,301 5,079 2,035 5.10 9.33 IE3 8,399 6,840 4,311 1,798 4.67 10.08 LLDPE1 8,568 6,864 4,138 1,655 5.18 9.64 LLDPE2 10,762 8,343 4,793 1,816 5.93 8.12 LLDPE3 6,665 6,313 5,037 2,432 2.74 34.34

TABLE 8 DSC Data T_(m1) T_(m2) T_(m3) Heat of Fusion T_(c1) T_(c2) Sample (° C.) (° C.) (° C.) (J/g) % Cryst. (° C.) (° C.) IE1 120.8 108.8 NA 135.2 46.3 108.8 98.2 IE2 119.3 107.6 NA 136.5 46.7 107.4 98.2 IE3 123.1 120.2 109.3 142.4 48.8 108.0 NA LLDPE1 123.4 121.5 109.0 142.7 48.9 108.0 NA LLDPE2 119.4 107.9 NA 139.6 47.8 107.1 98.2 LLDPE3 117.0 107.2 NA 140.0 47.9 105.1 NA

TABLE 9 Neutron Activation Data* Al Mg Ti V Hf Zr Cl Sample (ppm) (ppm) (ppm) (ppm) (ppb) (ppb) (ppm) IE1 46 570 1.1 1.56 ND@50 730 54 IE2 39 510 0.5 1.3 ND@50 790 47 IE3 22.6 43 1.4 2.6 ND@50 1110 89 *Niobium (Nb) (5 ppm), tantalum (Ta) (50 ppb), chromium (Cr) (0.5 ppm), molybdenum (Mo) (50 ppb), and tungsten (W) (5 ppm) were not detected in any of the examples at their respective detection limits, as indicated in the parentheses following each element. ND = not detected.

TABLE 10 1H NMR Data Total Unsatur- Vinylene/ Trisubstituted/ Vinyl/ Vinylidene/ ation/ Sample 1000C 1000C 1000C 1000C 1000C IE1 0.09 0.067 0.25  0.056 0.46 IE2 0.07 0.055 0.25  0.058 0.43 IE3 0.08 0.052 0.25  0.055 0.43 LLDPE1 0.06 0.036 0.24  0.046 0.39 LLDPE2 0.08 0.062 0.28  0.058 0.47 LLDPE3 0.08 0.085 0.097 0.027 0.29

FILM EXAMPLES

In the below Examples, IE1, IE2, IE3, LLDPE1, LLDPE2, and LLDPE3 are used to make different films as specified further for each Example. In addition, a low density polyethylene (identified as “LDPE” below) is also used. The LDPE is EB853/72 which is commercially available from Braskem and has a density of 0.922 g/cm³ and a melt index (I₂) of 1.00 g/10 min.

IE1, IE3, LLDPE1, and LLDPE3 each include 1000 ppm of a slip agent and 2500 ppm of an antiblock. IE2 includes 900 ppm of a slip agent and 2500 ppm of an antiblock. LLDPE2 includes 900 ppm of a slip agent and 5000 ppm of an antiblock.

Example 1

Inventive Film 1 and Comparative Film A are fabricated on a 3 layer blown film line using a 200 mm die diameter at a speed of 190 kg/hour and a blow up ratio (BUR) of 2.5. Each of the 3 layers has the same composition as shown in Table 11. The films have a nominal thickness of 50 microns. The Dart Impact (Method A), Elmendorf tear in the machine direction, and puncture resistance of the films are measured and the results are shown in Table 11.

TABLE 11 Dart Elmendorf Puncture Layer Impact Tear, MD Resistance Composition (grams) (grams) (J/cm³) Comparative 85% LLDPE1 417 834  9.3 Film A 15% LDPE Inventive 85% IE1 450 858 25.0 Film 1 15% LDPE

Inventive Film 1 using IE1 shows an improvement in dart impact and Elmendorf Tear, and a significant improvement in puncture resistance relative to Comparative Film A.

Example 2

Inventive Film 2 and Comparative Film B are fabricated on a 3 layer blown film line using a 450 mm die diameter at a speed of 420 kg/hour and a blow up ratio (BUR) of 2.5. Each of the 3 layers has the same composition as shown in Table 12. The films have a nominal thickness of 70 microns. The Dart Impact (Method A) and Elmendorf tear in the machine direction of the films are measured and the results are shown in Table 12.

TABLE 12 Dart Elmendorf Layer Impact Tear, MD Composition (grams) (grams) Comparative 80% LLDPE2 127 309 Film B 20% LDPE Inventive 80% IE2 361 432 Film 2 20% LDPE

Inventive Film 2 using IE2 shows a significant improvement in dart impact and Elmendorf Tear relative to Comparative Film B.

Example 3

Inventive Film 3 and Comparative Film C are fabricated on a monolayer blown film line using a 250 mm die diameter at a speed of 150 kg/hour and a blow up ratio (BUR) of 2.5. The films have the compositions shown in Table 13 and each has a nominal thickness of 70 microns. The Dart Impact (Method A), Elmendorf tear in the machine direction, and puncture resistance of the films are measured and the results are shown in Table 13.

TABLE 13 Dart Elmendorf Puncture Layer Impact Tear, MD Resistance Composition (grams) (grams) (J/cm³) Comparative 85% LLDPE1 386 1331 7.11 Film C 15% LDPE Inventive 85% IE3 392 1281 9.60 Film 3 15% LDPE

Inventive Film 3 using 1E3 shows comparable physical properties relative to Comparative Film C.

Example 4

Inventive Film 4 and Comparative Films D and E are fabricated on a monolayer blown film line using a 250 mm die diameter at a speed of 150 kg/hour and a blow up ratio (BUR) of 2.5. The films have the compositions shown in Table 14 and each has a nominal thickness of 70 microns. The Dart Impact (Method A), Elmendorf tear in the machine direction, and puncture resistance of the films are measured and the results are shown in Table 14.

TABLE 14 Dart Elmendorf Puncture Layer Impact Tear, MD Resistance Composition (grams) (grams) (J/m³) Comparative 80% LLDPE1 258 558 12.27 Film D 20% LDPE Comparative 80% LLDPE3 263 542 19.41 Film E 20% LDPE Inventive 80% IE1 311 560 25.43 Film 4 20% LDPE

Inventive Film 4 using IE1 shows improvement in dart impact and puncture resistance, and comparable Elmendorf Tear, relative to Comparative Film D and E. 

1. A film comprising a layer comprising: (a) 50% or more by weight or more of a polyethylene composition comprising the reaction product of ethylene and optionally one or more alpha-olefin comonomers, wherein said polyethylene composition is characterized by the following properties: a. a melt index, I₂, measured according to ASTM D 1238 (2.16 kg, 190° C.), of from 0.5 to 10 g/10 min; b. a density measured according to ASTM D792 of less than 0.935 g/cm³; c. a melt flow ratio, I₁₀/I₂, wherein I₁₀ is measured according to ASTM D1238 (10 kg, 190° C.) of from 6.0 to 7.5; d. a molecular weight distribution (M_(w)/M_(n)) of from 2.8 to 3.9; and e. a vinyl unsaturation of greater than 0.12 vinyls per one thousand carbon atoms; and (b) 50% or less by weight of a low density polyethylene.
 2. The film of claim 1, wherein the low density polyethylene has a melt index, 1₂, range of from 0.1-5 g/10 min.
 3. The film of claim 1, wherein the film comprises from 5-30% by weight of the low density polyethylene.
 4. The film of claim 1, wherein the film is a monolayer film.
 5. The film of claim 1, wherein the film is a multilayer film.
 6. The film of claim 1, wherein the polyethylene composition is formed in the presence of a catalyst composition comprising a multi-metallic procatalyst via solution polymerization in at least one reactor.
 7. The film of claim 6, wherein the solution polymerization occurs in a single reactor.
 8. The film of claim 6, wherein the polyethylene composition has a metal catalyst residual of greater than or equal to 1 parts by combined weight of at least three metal residues per one million parts of polyethylene polymer, wherein the at least three metal residues are selected from the group consisting of titanium, zirconium, hafnium, vanadium, niobium, tantalum, chromium, molybdenum, tungsten, and combinations thereof, and wherein each of the at least three metal residues is present at greater than or equal to 0.2 ppm.
 9. The film of claim 6, wherein the polyethylene composition has an Al:Ti ratio of from 6 to
 15. 10. An article made from the film according to claim
 1. 11. The article of claim 10, wherein the article is a pouch. 